Grain-oriented electrical steel sheet and magnetic domain refinement method therefor

ABSTRACT

A grain-oriented electrical steel sheet according to an exemplary embodiment of the present invention incudes a groove formed on a surface and a solidified alloy layer formed under the groove, wherein the solidified alloy layer includes recrystallized particles of which an average particle diameter is 1 to 8 μm.

TECHNICAL FIELD

A grain-oriented electrical steel sheet and a method for refiningmagnetic domains therein are related.

BACKGROUND ART

Since a grain-oriented electrical steel sheet is used as an iron corematerial of an electrical device such as a transformer, in order toimprove energy conversion efficiency thereof by reducing power loss ofthe device, it is necessary to provide a steel sheet having excellentiron loss of the iron core material and a high occupying ratio whenbeing stacked and spiral-wound.

The grain-oriented electrical steel sheet refers to a functionalmaterial having a texture (referred to as a “GOSS texture”) of which asecondary-recrystallized grain is oriented with an azimuth {110}<001> ina rolling direction through a hot rolling process, a cold rollingprocess, and an annealing process.

A permanent magnetic domain refining method which shows the improvementof the iron loss even after a stress relaxation heat treatment above aheat treatment temperature where recovery occurs may be divided into anetching method, a roll method, and a laser method. Since it is difficultto control a groove shape because the grooves are formed on the surfaceof the steel sheet by a selective electrochemical reaction in asolution, it is difficult to uniformly secure the iron losscharacteristics of the final product in the width direction. Inaddition, an acid solution used as a solvent has a disadvantage that itis not environmentally friendly.

The method of refining the permanent magnetic domain by the roll is atechnology of magnetic domain miniaturization partially generatingrecrystallized particles under the groove by forming and then annealinga groove having a constant width and depth on the surface of the plateby processing a protrusion shape on the roll to be pressed by the rollor the plate. The roll method is disadvantageous in stability in machineprocessing, reliability to obtain stable iron loss depending on thethickness, and process complexity, and deterioration of the iron lossand the magnetic flux density characteristics immediately after thegroove formation (before the stress relaxation annealing).

As the method of refining the permanent magnetic domain by a laser of apulse and non-Gaussian mode forms a solidified alloy layer of the groovepart only at the side wall or does not uniformly form the groove on theentire surface of the groove when forming the groove, because of causingexcessive deformation at the bottom part of the groove, it is difficultto apply to the process before the primary recrystallization process orafter the primary recrystallization process and it has a drawback thatit shows a deteriorated occupying ratio after a final insulationcoating. The grooving method by a continuous wave laser may form thesolidified alloy layer entirely or partially, however it has a drawbackthat it is difficult to control the recrystallized particles' grain sizein the heat treatment condition above the stress relaxation annealingthrough the thickness control of the solidified alloy layer.

DISCLOSURE Technical Problem

A grain-oriented electrical steel sheet having an iron loss improvementand a low magnetic flux density degradation rate characteristic after aheat treatment and a method for refining a magnetic domain therein areprovided.

Technical Solution

A grain-oriented electrical steel sheet according to an exemplaryembodiment of the present invention includes: a groove formed on asurface; and a solidified alloy layer formed under the groove, whereinthe solidified alloy layer includes recrystallized particles of which anaverage particle diameter is from 1 to 10 μm.

A grain-oriented electrical steel sheet according to another exemplaryembodiment of the present invention includes: a groove formed on asurface; and a solidified alloy layer formed under the groove, whereinthe solidified alloy layer includes recrystallized particles of which anaverage particle diameter is from 1 to 20 μm after stress relaxationannealing.

A thickness of the solidified alloy layer may be 0.6 to 3.0 μm.

A non-metallic oxide layer formed on the surface of the electrical steelsheet may be further included.

The non-metallic oxide layer may include Mg₂SiO₄, Al₂SiO₄, or Mn₂SiO₄.

An insulating coating layer formed on the non-metallic oxide layer maybe further included.

The groove may be linear and may be formed with an angle of 82° to 98°with respect to a rolling direction of the electrical steel sheet.

A depth D of the groove may be from 3% to 8% of the thickness of theelectrical steel sheet.

A magnetic domain refining method of a grain-oriented electrical steelsheet according to an exemplary embodiment of the present inventionincludes: preparing a grain-oriented electrical steel sheet; irradiatinga laser to a surface of the grain-oriented electrical steel sheet toform a groove; and quenching a portion where the groove is formed with acooling speed of 400 to 1500° C./s.

The quenching may be simultaneous quenching with the groove formation.

Stress relaxation annealing after the quenching may be further included.

In the groove forming, the laser may be a continuous wave laser having aGaussian energy distribution and an output of 1 kW or more.

The laser may be a continuous wave laser that is a TEM₀₀ mode and has abeam quality factor M² of 1.0 to 1.1 and an output of 1 to 10 kW.

Removing a hill-up or a spatter formed on the electrical steel sheetsurface after forming the groove may be further included.

Preparing the grain-oriented electrical steel sheet may include: formingan oxide layer on the surface of the steel sheet bydecarburization-annealing or nitriding-annealing the cold-rolled steelsheet; and forming a non-metallic oxide layer on the surface of thesteel plate by coating an annealing separator on the surface of thesteel plate on which the oxidation layer is formed.

After forming the non-metallic oxide layer, forming an insulatingcoating layer on the non-metallic oxide layer may be further included.

Advantageous Effects

According to one embodiment of the present invention, the magnetic fluxdensity degradation due to permanent magnetic domain refining may bereduced and the iron loss improvement rate may be increased.

Also, according to one embodiment of the present invention, it may beused as a stacked iron core transformer and a wound iron coretransformer iron core requiring a heat treatment after the finalinsulation coating.

DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic view of a grain-oriented electrical steel sheetaccording to an exemplary embodiment of the present invention.

FIG. 2 is a cross-sectional schematic view of a grain-orientedelectrical steel sheet according to an exemplary embodiment of thepresent invention.

FIG. 3 is a cross-sectional schematic view of a grain-orientedelectrical steel sheet according to another exemplary embodiment of thepresent invention.

FIG. 4 is a cross-sectional schematic view of a grain-orientedelectrical steel sheet according to another exemplary embodiment of thepresent invention.

MODE FOR INVENTION

The terms “first”, “second”, and “third” are used herein to explainvarious parts, components, regions, layers, and/or sections, but itshould be understood that they are not limited thereto. These terms areused only to discriminate one portion, component, region, layer, orsection from another portion, component, region, layer, or section.Thus, a first portion, component, region, layer, or section may bereferred to as a second portion, component, region, layer, or sectionwithout departing from the scope of the present invention.

The technical terms used herein are to simply mention a particularembodiment and are not meant to limit the present invention. Anexpression used in the singular encompasses the expression of theplural, unless it has a clearly different meaning in the context. Theterm ‘including’ used herein embodies concrete specific characteristics,regions, positive numbers, steps, operations, elements, and/orcomponents, without limiting existence or addition of other specificcharacteristics, regions, positive numbers, steps, operations, elements,and/or components.

It will be understood that when an element such as a layer, film,region, or substrate is referred to as being “on” or “above” anotherelement, it can be directly on or above the other element or interveningelements may also be present. In contrast, when an element is referredto as being “directly on” another element, there are no interveningelements therebetween.

If not defined differently, all the terminologies including technicalterminologies and scientific terminologies used herein have meaningsthat are the same as ones that those skilled in the art generallyunderstand. The terms defined in dictionaries should be construed ashaving meanings corresponding to the related prior art documents andthose stated herein, and are not to be construed as being ideal orofficial, if not so defined.

Hereinafter, exemplary embodiments of the present invention will bedescribed in detail so as to be easily practiced by a person skilled inthe art to which the present invention pertains. As those skilled in theart would realize, the described embodiments may be modified in variousdifferent ways, all without departing from the spirit or scope of thepresent invention.

FIG. 1 shows a schematic view of a grain-oriented electrical steel sheet10 according to an exemplary embodiment of the present invention. Asshown in FIG. 1, a plurality of grooves 20 are formed along a rollingdirection on the surface of the grain-oriented electrical steel sheet10.

FIG. 2 shows a cross-sectional schematic view of a grain-orientedelectrical steel sheet 10 according to an exemplary embodiment of thepresent invention. As shown in FIG. 2, the grain-oriented electricalsteel sheet 10 according to an exemplary embodiment of the presentinvention includes the groove 20 formed on the surface and a solidifiedalloy layer 30 formed under the groove 20, and the solidified alloylayer 30 includes recrystallized particles 31 having an average particlediameter of 1 to 10 μm. In an exemplary embodiment of the presentinvention, by controlling the size of the recrystallized particles 31 inthe solidified alloy layer 30, although a heat treatment above arecrystallization temperature such as a stress relaxation annealing isapplied, an improvement effect of the iron loss may be obtained evenafter stress relaxation annealing as a recrystallized grain is grown inthe solidified alloy layer 30 and into the base. The average particlediameter of the recrystallized particles 31 may be 1 to 10 μm. If theaverage particle diameter of the recrystallized particles 31 is toosmall, the magnetic flux density degradation rate is increased due tothe increase in the semi-magnetic field. If the average particlediameter of the recrystallized particles 31 is too large, due to thereduction of the semi-magnetic field, the iron loss improvement rate isdecreased and the magnetic flux density degradation rate is increased.More specifically, the average particle diameter of the recrystallizedparticles 31 may be in a range of 2 to 7 μm.

FIG. 3 shows a cross-section of the grain-oriented electrical steelsheet 10 according to another exemplary embodiment of the presentinvention. When the grain-oriented electrical steel sheet 10 in FIG. 2described above is heat-treated above the recrystallization temperaturesuch as in the stress relaxation annealing, the recrystallized grain isgrown in the inner part of the solidified alloy layer 30, and the baseportion and recrystallized particles 32 are formed after the stressrelaxation annealing. The recrystallized particles 32 formed after thestress relaxation annealing may have an average particle diameter of 1to 20 μm.

The solidified alloy layer 30 is formed during laser irradiation forrefining the magnetic domain. The thickness of the solidified alloylayer 30 may be between 0.6 and 3.0 μm. When the thickness of thesolidified alloy layer 30 is very thin, since the recrystallizedparticles 31 in the solidified alloy layer 30 are not grown to the baseportion in which the secondary recrystallization occurs, the iron lossimprovement effect by the recrystallized particles 31 does not occur,and when the thickness of solidified alloy layer 30 is too thick, therecrystallized particles 32 are formed, but the recrystallized particles32 after stress relaxation annealing are also formed at the lowerportion, the side portion, and the base portion by a heat effect, andaccordingly the magnetic flux density deterioration may becomeremarkable.

As shown in FIG. 4, a non-metallic oxide layer 40 may be formed on thesurface of the steel plate 10. When the non-metallic oxide layer 40 isformed, a laser absorption rate is increased by 30% or more compared tothat of the steel plate in which the non-metallic oxide layer 40 is notformed when irradiating the laser, so the grooves 20 may be formed withrelatively low energy density, and the linear grooves 20 may be formedwith a high irradiation speed.

Accordingly, a laser output required for forming the groove 20 isreduced by 20% or more for the steel plate on which the non-metallicoxide layer 40 is formed compared with the steel plate on which thenon-metallic oxide layer 40 is not formed, thereby increasing theefficiency in improving the iron loss.

In addition, when the non-metallic oxide layer 40 is formed on thesurface of the steel plate, the non-metallic oxide layer is physicallyand chemically solid-bonded to the steel plate surface and is not easilydamaged by thermal impact by laser irradiation.

Preferably, the non-metallic oxide layer 40 is formed on the surface ofthe steel plate with a thickness of 1 to 20 μm. If the thickness of thenon-metallic oxide layer 40 is too thin, the effect of increasing thelaser absorption rate is low and the non-metallic oxide layer may bedestroyed by the thermal impact during the laser irradiation, and if thethickness of the non-metallic oxide layer 40 is too thick, there isdrawback that it is difficult to control the process conditions forforming the non-metallic oxide layer 40 and the laser output for formingthe groove 20 is increased.

The non-metallic oxide layer 40 may comprise Mg₂SiO₄, Al₂SiO₄, orMn₂SiO₄.

An insulating coating layer 50 may be formed on the non-metallic oxidelayer 40.

The depth D of groove 20 may be 3% to 8% of the thickness of theelectrical steel sheet. More specifically, it may be 4% to 8%. If it isless than 3%, the groove of an appropriate depth for improving the ironloss is not formed. If it exceeds 8%, a heat affected part may increaseand the growth of the Goss texture may have an adverse effect.

In addition, the groove 20 may be formed at 82° to 98° with respect tothe rolling direction of the electrical steel sheet. By forming thegroove 20 in an oblique shape not including 90 degrees, thesemi-magnetic field may be weakened, thereby improving the magnetism.

The grooves 20 may be formed intermittently from 2 to 10 pieces in thewidth direction of the steel plate.

The magnetic domain refining method of the grain-oriented electricalsteel sheet according to an exemplary embodiment of the presentinvention includes: preparing the grain-oriented electrical steel sheet;irradiating a laser to the surface of the grain-oriented electricalsteel sheet to form the groove; and quenching the part where the grooveis formed at a cooling speed of 400 to 1500° C./s. Hereinafter, eachstep is described in detail.

First, the grain-oriented electrical steel sheet is prepared.

The preparation of the grain-oriented electrical steel sheet mayinclude: decarbonizing or nitriding a cold-rolled electrical steel sheetto form an oxidation layer on the surface of the steel plate; andcoating an annealing separator on the surface of the steel plate onwhich the oxidation layer is formed and annealing at a high temperatureto form a non-metallic oxide layer on the surface of the steel plate.

Generally, the cold-rolled steel sheet may be produced by subjecting aslab containing 1 to 7% by weight of Si to hot rolling, hot-rolled sheetannealing, and cold rolling. Since the non-metallic oxide layer is thesame as described above, repeated description is omitted.

In an exemplary embodiment of the present invention, the magnetic domainrefining may be performed directly on the surface of the steel plate, orthe non-metallic oxide may be formed on the surface of the steel plate,magnetic domain refining and then the laser may be irradiated to performthe magnetic domain refining, and an insulating coating layer may beadditionally formed on the surface of the steel plate by coating andheat-treating an insulating coating liquid including colloidal silicaand a metal phosphate on the non-metallic oxide layer and then the lasermay be irradiated to perform the magnetic domain refining. If thenon-metallic oxide layer is formed on the surface of the steel plate,this layer may increase the laser absorption rate and form the groovewith relatively low energy density.

Next, the surface of the grain-oriented electrical steel sheet isirradiated with the laser to form the groove.

At this time, the laser may be a continuous wave laser having a Gaussianenergy distribution and an output of 1 kW or more. This continuous wavelaser is suitable for forming the uniform groove on the electrical steelsheet surface after the secondary recrystallization is completed. Morespecifically, the laser is a TEM₀₀ mode, and may be a continuous wavelaser of which a beam quality factor M2 is 1.0 to 1.1 and the output is1 to 10 kW. Since forming grooves with a gasify only by the laserirradiation does not form the solidified alloy layer, the method offorming the groove using the laser with too high an output is notpreferable.

A step of removing a hill-up or a spatter formed on the electrical steelsheet surface after the step of forming the groove may be furtherincluded. The heel-up means that a fusion material generated during thegroove formation has risen to the both tops of the groove, and thespatter is formed by scattering of the fusion material. The hill-up andthe spatter may be removed by brushing or pickling.

Next, the portion where the groove is formed is quenched at a coolingspeed of 400 to 1500° C./s. In an exemplary embodiment of the presentinvention, the size of the recrystallized particles in the solidifiedalloy layer may be controlled by controlling the cooling speed.Specifically, the average particle diameter of the recrystallizedparticles in the solidified alloy layer may be controlled from 1 to 10μm by controlling the cooling speed from 400 to 1500° C./s. Morespecifically, the cooling speed may be adjusted from 500 to 1200° C./s.

The quenching method is not particularly limited, and an air coolingmethod above the laser irradiation may be used. The quenching steps maybe done simultaneously with the groove formation.

After the quenching, the stress relaxation annealing may be furtherincluded. In case of the heat treatment above the recrystallizationtemperature such as the stress relaxation annealing in an exemplaryembodiment of the present invention, the recrystallized grain grows inthe solidified alloy layer and to the base portion such thatrecrystallized particles are formed after the stress relaxationannealing. The recrystallized particles after the stress relaxationannealing may have the average particle diameter of 1 to 20 μm.

In this heat treatment condition above the recrystallization temperatureafter the formation of the solidified alloy layer, the recrystallizedparticle formation after the stress relaxation annealing may achieve animprovement effect of the iron loss of 2% or more and simultaneously amagnetic flux density degradation rate of 1.0% or less.

Hereinafter, the present invention is described in more detail throughan example. However, this example is merely to illustrate the presentinvention, and the present invention is not limited thereto.

EXAMPLE

The grain-oriented electrical steel sheet of the cold-rolled thicknessof 0.30 mm is decarburization-annealed to form the oxidation layer, theannealing separator including MgO is coated, and the high temperatureannealing is performed to form a forsterite film. Thereafter, theinsulating coating liquid containing the colloidal silica and the metalphosphate is coated to form the insulating coating layer.

That laser that is a TEM₀₀ mode and has the beam quality factor of M² of1.0 is irradiated to the electrical steel sheet surface by controllingthe output to 1.8 kW. In a case of Comparative Example 2 of Table 2, apulse laser that is not a continuous wave laser is used. During thelaser irradiation, the cooling speed is adjusted as shown in thefollowing table through the air cooling. After the magnetic domainrefinement treatment, the stress annealing is performed.

The groove depth, the solidified alloy layer thickness, the averageparticle diameter of the recrystallized particles in the solidifiedalloy layer, and the recrystallized particle average particle diameterof the stress annealing are summarized in Table 1 and Table 2.

TABLE 1 Recrystallized particles Recrystallized After heat Solidifiedaverage particles average treatment Magnetic Groove alloy layer particleparticle diameter Before laser After laser stress Iron loss flux densitydepth thickness diameter after stress irradiation irradiation annealingimprovement degradation (μm) (μm) (μm) annealing W_(17/50)/B₈ rate (%)rate (%) Example 9 0.6 6 8 0.96/1.92 0.86/1.91 0.83/1.91 3.5 0.0(continuous 9 0.97/1.92 0.86/1.91 0.84/1.91 2.3 0.0 wave/cooling 3.0 913 0.97/1.92 0.87/1.91 0.82/1.90 5.7 −0.5 speed 15 0.96/1.92 0.86/1.910.81/1.90 5.8 −0.5 500° C./s) 18 0.6 5 9 0.96/1.92 0.85/1.91 0.81/1.902.4 −0.5 10 0.96/1.92 0.86/1.91 0.82/1.91 2.3 0.0 3.0 7 14 0.97/1.920.85/1.90 0.82/1.89 3.5 −0.5 16 0.96/1.92 0.87/1.91 0.83/1.90 4.6 −0.5

TABLE 2 Recrystallized After particle Recrystallized stress Solidifiedaverage particles average annealing Magnetic Groove alloy layer particleparticle diameter Before laser After laser heat Iron loss flux densitydepth thickness diameter after stress irradiation irradiation treatmentimprovement degradation Occupying (μm) (μm) (μm) annealing (μm)W_(17/50)/B₈ rate (%) rate (%) ratio (%) Example 15 3.0 7.0 11 0.97/1.920.85/1.90 0.82/1.90 3.5 0.0 97.2 (continuous 12 0.97/1.92 0.85/1.900.82/1.90 2.4 0.0 97.1 wave/ cooling speed. 500° C./s) Example 15 0.62.0 9 0.97/1.92 0.85/1.90 0.81/1.90 4.7 0.0 97.3 (continuous 9 0.97/1.920.84/1.90 0.80/1.90 5.9 0.0 97.4 wave/ cooling speed. 1200° C./s)Comparative 15 3.5 8.7 21 0.97/1.92 0.93/1.89 0.93/1.87 0.0 −1.05 95.1Example 1 22 0.96/1.92 0.92/1.89 0.92/1.87 0.0 −1.05 95.2 (continuouswave/ cooling speed. 300° C./s) Comparative 15 0.3 No formation —0.97/1.92 1.01/1.87 1.01/1.85 0.0 −1.06 94.8 Example 2 — 0.96/1.920.99/1.86 0.99/1.85 0.0 −0.53 94.7 (Pulse Laser/ cooling speed 500°C./s)

In Table 1 and Table 2, the iron loss improvement rate is calculated by(W₁-W₂)/W₁ by measuring the iron loss W₁ of the electrical steel sheetbefore the groove is formed by the laser irradiation and the iron lossW₂ after forming the groove by the laser irradiation. The magnetic fluxdensity degradation rate is calculated by (B₂-B₁)/B₁ by measuring themagnetic flux density B₁ of the electrical steel sheet before the grooveis formed by the laser irradiation and the magnetic flux density B₂after forming the groove by the laser irradiation. The occupying ratioas a weight ratio of the steel plate corresponding to an actual volumefor a theoretical volume under a 5 MPa pressure is measured by a methodof JIS C 2550-2000.

As shown in Table 1 and Table 2, in an example in which the continuouswave laser is used and the cooling speed is appropriately adjusted, itmay be confirmed that the recrystallized particles are formed with theappropriate size in the solidified alloy layer, the iron lossimprovement rate and the magnetic flux density degradation rate areexcellent, and the iron loss and the magnetic flux density are excellenteven after the stress annealing heat treatment.

Although exemplary embodiments of the present invention were describedwith reference to the accompanying drawings, the present invention isnot limited to the exemplary embodiments and may be modified in variousways. Further, it would be understood that the present invention may beimplemented in other detailed ways by those skilled in the art withoutthe scope and necessary components of the present invention beingchanged. Therefore, the embodiments described above are only examplesand should not be construed as being !imitative in all respects.

<Description of symbols> 10: electrical steel sheet 20: groove 30:solidified alloy layer 31: recrystallized particles 32: recrystallizedparticles after 40: non-metallic oxide stress annealing layer 50:insulating coating layer

1. A grain-oriented electrical steel sheet comprising: a groove formed on a surface of an electrical steel sheet; and a solidified alloy layer formed under the groove, wherein the solidified alloy layer includes recrystallized particles of which an average particle diameter is from 1 to 10 μm.
 2. A grain-oriented electrical steel sheet comprising: a groove formed on a surface of an electrical steel sheet; and a solidified alloy layer formed under the groove, wherein the solidified alloy layer includes recrystallized particles of which an average particle diameter is from 1 to 20 μm after stress relaxation annealing.
 3. The grain-oriented electrical steel sheet of claim 1, wherein a thickness of the solidified alloy layer is 0.6 to 3.0 μm.
 4. The grain-oriented electrical steel sheet of claim 1, further comprising a non-metallic oxide layer formed on the surface of the electrical steel sheet.
 5. The grain-oriented electrical steel sheet of claim 4, wherein the non-metallic oxide layer includes Mg₂SiO₄, Al₂SiO₄, or Mn₂SiO₄.
 6. The grain-oriented electrical steel sheet of claim 4, further comprising an insulating coating layer formed on the non-metallic oxide layer.
 7. The grain-oriented electrical steel sheet of claim 1, wherein the groove is linear and is formed at an angle of 82° to 98° with respect to a rolling direction of the electrical steel sheet.
 8. The grain-oriented electrical steel sheet of claim 1, wherein a depth D of the groove is from 3% to 8% of the thickness of the electrical steel sheet.
 9. A magnetic domain refining method of a grain-oriented electrical steel sheet, comprising: preparing a grain-oriented electrical steel sheet; irradiating a laser to a surface of the grain-oriented electrical steel sheet to form a groove; and quenching a portion where the groove is formed with a cooling speed of 400 to 1500° C./s.
 10. The magnetic domain refining method of the grain-oriented electrical steel sheet of claim 9, wherein the quenching is simultaneous quenching with the groove formation.
 11. The magnetic domain refining method of the grain-oriented electrical steel sheet of claim 9, further comprising, after the quenching, stress relaxation annealing.
 12. The magnetic domain refining method of the grain-oriented electrical steel sheet of claim 9, wherein, in the forming of the groove, the laser is a continuous wave laser having a Gaussian energy distribution and an output of 1 kW or more.
 13. The magnetic domain refining method of the grain-oriented electrical steel sheet of claim 12, wherein the laser is a continuous wave laser that is a TEM₀₀ mode and has a beam quality factor of M² of 1.0 to 1.1 and output of 1 to 10 kW.
 14. The magnetic domain refining method of the grain-oriented electrical steel sheet of claim 9, further comprising removing a hill-up or a spatter formed on the electrical steel sheet surface after forming the groove.
 15. The magnetic domain refining method of the grain-oriented electrical steel sheet of claim 9, wherein the preparing the grain-oriented electrical steel sheet includes: forming an oxide layer on the surface of the steel sheet by decarburization-annealing or nitriding-annealing the cold-rolled steel sheet; and forming a non-metallic oxide layer on the surface of the steel plate by coating an annealing separator on the surface of the steel plate on which the oxidation layer is formed.
 16. The magnetic domain refining method of the grain-oriented electrical steel sheet of claim 15, further comprising, after forming the non-metallic oxide layer, forming an insulating coating layer on the non-metallic oxide layer. 